Product made of an alcumg alloy for aircraft structural elements

ABSTRACT

Rolled, extruded or forged product made of an AlCuMg alloy processed by solution heat treatment, quenching and cold stretching, to be used in the manufacture of aircraft structural elements, with the following composition (% by weight):  
                                                   Fe&lt;0.15   Si&lt;0.15   Cu:3.8-4.4   Mg:1-1.5         Mn:0.5-0.8   Zr:0.08-0.15                               
 
     other elements: &lt;0.05 each and &lt;0.15 total with a ratio R m (L)/R 0.2  (L)&gt;1.25.  
     The invention is particularly applicable to the manufacture of lower wings, and has a set of properties (toughness, crack propagation rate, fatigue strength, residual stress level), that are better than alloy 2024.

TECHNICAL FIELD

[0001] This invention relates to rolled, extruded or forged products made of a quenched and stretched AlCuMg alloy designed for the manufacture of aircraft structural elements, particularly skin panels and lower wing stringers, and with an improved compromise between mechanical strength, formability, toughness, tolerance to damage and residual stress properties than is available with products according to prior art used for the same application. Designations of alloys and metallurgical tempers are in accordance with the terminology used by the Aluminum Association, and repeated in European standards EN 515 and EN 573.

[0002] Temper of Prior Art

[0003] Wings for high capacity commercial aircraft comprise an upper part (upper wing) composed of a skin made of thick 7150 alloy plates in tempers T651, or 7055 alloy plates in temper T7751 or 7449 alloy plates in temper T7951, and stringers made from profiles of the same alloy, and a lower part (lower wing) composed of a skin made of thick plates made of a 2024 alloy in temper T351 or a 2324 alloy in temper T39, and stringers made from profiles of the same alloy. The two parts are assembled by spars and ribs.

[0004] The chemical composition of 2024 alloy according to the terminology used by the Aluminum Association and standard EN 573-3 is as follows (% by weight):

[0005] SI<0.5

[0006] Fe<0.5

[0007] Cu: 3.8-4.9

[0008] Mg: 1.2-1.8

[0009] Mn: 0.3-0.9

[0010] Cr<0.10

[0011] Zn<0.25

[0012] Ti<0.15

[0013] Different variants have been developed and registered with the Aluminum Association as 2224, 2324 and 2424, particularly with lower contents of silicon and iron. Alloy 2324 in temper T39 was described in Boeing patent EP 0038605 (U.S. Pat. No. 4,294,625), in which the improvement to the yield stress is obtained by work hardening by a cold rolling pass after quenching. This work hardening tends to reduce the toughness, and the contents of Fe, Si, Cu and Mg are reduced in order to compensate the drop in toughness. Boeing also developed alloy 2034 with composition:

[0014] Si<0.10

[0015] Fe<0.12

[0016] Cu: 4.2-4.8

[0017] Mg: 1.3-1.9

[0018] Mn: 0.8-1.3

[0019] Cr<0.05

[0020] Zn<0.20

[0021] Ti<0.15

[0022] Zr: 0.08-0.15

[0023] This alloy is described in patent EP 0031605 (U.S. Pat. No. 4,336,075). Compared with alloy 2024 in temper T351, it has a better specific yield stress due to an increase in the manganese content and the addition of another anti-recrystallizing agent (Zr), and also has improved toughness and fatigue strength.

[0024] Alcoa patent EP 0473122 (U.S. Pat. No. 5,213,639) describes an alloy, recorded by the Aluminum Association as 2524, with composition:

[0025] Si<0.10

[0026] Fe<0.12

[0027] Cu: 3.8-4.5

[0028] Mg: 1.2-1.8

[0029] Mn: 0.3-0.9

[0030] that can also contain an other anti-recrystallizing agent (Zr, V, Hf, Cr, Ag or Sc). This alloy is intended specifically for thin plates for fuselages and its toughness and resistance to crack propagation are improved compared with 2024.

[0031] Patent application EP 0731185 made by the applicant relates to an alloy, subsequently registered as 2024A with composition:

[0032] Si<0.25

[0033] Fe<0.25

[0034] Cu: 3.5-5

[0035] Mg: 1-2

[0036] Mn<0.55

[0037] The thick plates made of this alloy are tougher and residual stresses are lower, without any loss of other properties.

[0038] Alcoa patents U.S. Pat. No. 5,863,359 and U.S. Pat. No. 5,865,914 relate to an aircraft wing with a lower wing made of an alloy with composition:

[0039] Cu: 3.6-4

[0040] Mg: 1-1.6 (preferably 1.15-1.5)

[0041] Mn: 0.3-0.7 preferably 0.5-0.6),

[0042] Zr: 0.05-0.25 and preferably

[0043] Fe<0.07 and

[0044] Si<0.05

[0045] Mn:0.3-0.7 preferably 0.5-0.6), Zr:0.05-0.25 and preferably Fe<0.07 and Si <0.05 with the following properties:

[0046] R₀ ₂(LT)>60 ksi (414 MPa) and K_(ie)(L-T)>38 ksi{square root}inch (42 MPa{square root}m),

[0047] and a process for manufacturing a lower wing element with R_(0.2)(LT)>60ksi comprising casting of an alloy with the previous composition, homogenization between 471 and 482° C., hot transformation at a temperature >399° C.; solution heat treatment above 488° C., quenching cold work hardening preferably by more than 9% and stretching by at least 1%.

[0048] Problem that Arises

[0049] One essential constraint when constructing new high capacity commercial aircraft is to limit the weight, such that manufacturer specifications impose higher typical stresses for wing panels, which leads to higher minimum values for static mechanical properties and higher damage tolerance for the aluminum alloy products used. The use of work hardened products in temper T39, as recommended in U.S. Pat No. 5,863,359 and U.S. Pat. No. 5,865,914, does give higher yield stresses R_(0.2), but it also has a number of disadvantages for other working properties that are important in this application. One result is a very small plastic range, in other words the difference between the ultimate stress R_(m) and the yield stress R_(0.2), which results in lower cold formability and less resistance to crack propagation under a load with a variable amplitude. The reduction in the rate of crack propagation after a partial overload is less important if the plastic range is small.

[0050] Furthermore, large parts must be machined without distortion in thicker plates, which requires better control of residual stresses. However, temper T39 is not particularly advantageous from this point of view.

[0051] Therefore the purpose of this invention is to provide AlCuMg alloy products in the work hardened and cold deformed temper, for use in manufacturing aircraft lower wings, and providing a better compromise of all working properties (mechanical strength, rate of crack propagation, toughness, resistance to fatigue and residual stresses) than is possible with similar products according to prior art.

[0052] Purpose of the Invention

[0053] The purpose of the invention is a rolled, extruded or forged product made of an AlCuMg alloy processed by solution heat treatment, quenching and cold stretching, to be used in the manufacture of aircraft structural elements, with the following composition (% by weight):

[0054] Fe<0.15

[0055] Si<0.15

[0056] Cu: 3.8-4.4 (preferably: 4.0-4.3)

[0057] Mg: 1.0-1.5

[0058] Mn: 0.5-0.8

[0059] Zr: 0.08-0.15

[0060] other elements: <0.05 each and <0.15 total with a ratio R_(m)(L)/R_(0.2) (L) of the ultimate tensile strength in the L direction to the yield stress in the L direction exceeding 1.25 (and preferably exceeding 1.30).

[0061] Another purpose is a rolled product (plate) with the same composition and between 6 and 60 mm thick and with at least the following groups of properties in the quenched and stretched temper:

[0062] a) Ultimate tensile strength R_(m(L))>475 MPa and yield stress R_(0.2(L))>370 MPa

[0063] b) Plastic range R_(m)-R_(0.2) in the L and TL directions >100MPa.

[0064] c) Critical intensity factor (L-T direction) K_(c)>170MPa{square root}m and K_(co)>120 MPa{square root}m (measured according to ASTM standard E 561 on notched test pieces sampled at a quarter thickness with parameters B=5 mm, W=500 and 2_(B0)=165 mm)

[0065] d) Crack propagation rate (L-T direction) da/dn, measured according to ASTM standard E 647 on notched test pieces sampled at a quarter thickness with parameters W=200 mm and B =5 mm)

[0066] <10⁻⁴ mm/cycle for ΔK=10 MPa{square root}m

<2.5 10⁻⁴ mm/cycle for ΔK=15 MPa{square root}m

and <5 10⁻⁴ mm/cycle for ΔK=20 MP{square root}m

[0067] This plate also has residual stresses such that the deflection f measured in the L and TL directions after machining a bar supported on two supports separated by a length 1 to its mid-thickness, is such that:

[0068] f<(0.14 1²)/e, where f is measured in microns, e is the thickness of the plate and 1 is the length measured in mm.

[0069] Another purpose of the invention is a process for manufacturing a rolled, extruded or forged product comprising the following steps:

[0070] cast a plate or billet with the indicated composition,

[0071] homogenize this plate or billet between 450 and 500° C.,

[0072] hot transformation, and possibly cold transformation, until the required product is obtained,

[0073] solution heat treatment at a temperature of between 480 and 505° C.,

[0074] quench in cold water,

[0075] cold stretching to at least 1.5% permanent deformation,

[0076] natural aging under ambient conditions.

DESCRIPTION OF THE INVENTION

[0077] The chemical composition of the product is different from the chemical composition of the usually used 2024 in that the iron and silicon contents are lower, the manganese content is higher, and zirconium is added. Compared with 2034, the magnesium content is lower and the copper content is slightly lower. Compared with the composition of the alloys described in U.S. Pat. No. 5,863,359 and U.S. Pat. No. 5,865,914, the copper content is higher, compensating the lower work hardening after quenching, for the mechanical strength. Surprisingly, this narrow composition range (particularly for manganese) combined with modifications to the manufacturing procedure, can give a significant improvement in the compromise between the mechanical strength, elongation and damage tolerance under operating conditions for a high capacity civil aircraft, compared with prior art. Furthermore, and quite unexpectedly, low residual stresses are observed particularly for thick products, so that large parts can be machined without distortion.

[0078] The manufacturing process consists of casting the plates in the case in which the product to be made is a rolled plate, or the billets in the case of an extruded profile or forged part. The plate or the billet is scalped and then homogenized at between 450 and 500° C. The hot transformation is then made by rolling, extrusion or forging. This transformation is preferably made at a temperature higher than temperatures normally used, the output temperature being greater than 420° C. and preferably greater than 440° C. so that the treated product has a slightly recrystallized structure, with a recrystallization rate of less than 20%, and preferably less than 10%, at a quarter thickness. The rolled, extruded or forged semi-product is then put into solution heat treatment at between 480 and 505° C., such that solution heat treatment is as complete as possible, in other words that the maximum number of potentially soluble phases, and particularly Al₂Cu and Al₂CuMg precipitates, are actually in solid solution. The quality of the solution heat treatment may be evaluated by differential enthalpic analysis (AED) by measuring the specific energy using the area of the peak on the thermogram. This specific energy must preferably be less than 2 J/g.

[0079] Quenching is then done with cold water, followed by controlled stretching to give a permanent elongation of not less than 1.50%. Finally, the product is aged naturally at ambient temperature.

[0080] Products according to the invention have significantly improved static mechanical properties compared with alloy 2024-T351, currently used for aircraft lower wings, and only slightly lower than the properties of 2034-T351. The high plastic range and elongation of the material give excellent cold formability. The toughness, measured by critical stress intensity factors in plane stress K_(c) and K_(co) is greater than the toughness of 2024 and 2034 by more than 10%, and the crack propagation rate da/dn is significantly better than these two alloys, particularly for high values of ΔK, and for loads with variable amplitude. Fatigue lives measured on notched samples taken at mid-thickness in the L direction are also more than 20% better than with 2024 and 2034. Finally, the magnitude of residual stresses measured by the deflection f after machining a bar supported on two supports separated by distance 1 to half its thickness, is fairly low, although the opposite might have been expected with a fibrous structure. This deflection, measured in microns, is always less than the quotient (0.14 1²)/e, where the length 1 and the thickness e of the plate are expressed in mm.

[0081] All these properties mean that products according to the invention are particularly suitable for manufacturing aircraft structural elements, particularly lower wings, but also profiles for a wing spar box, assembled spar booms and rib flanges and fuselage skins and stringers.

EXAMPLES

[0082] Three 1450 mm wide and 446 mm thick plates were cast, made of 2024, 2034 alloys and the alloy according to the invention, respectively. The chemical compositions (% by weight) of the alloys are as given in Table 1: TABLE 1 Alloy Si Fe Cu Mg Mn Zr 2024 0.12 0.20 4.06 1.36 0.54 0.002 2034 0.05 0.07 4.30 1.34 0.98 0.104 Invention 0.06 0.08 4.14 1.26 0.65 0.102

[0083] The plates were scalped, and then homogenized under the following conditions:

[0084] For the 2024, 2 h at 495° C. then 5 h at 460° C.

[0085] For the 2034, 5 h at 497° C.

[0086] For the alloy according to the invention, the temperature was increased in 12 h and kept for 6 h at 483° C.

[0087] A part of the plates was then hot rolled to a thickness of 40 mm by successive passes of the order of 20 mm. Another part of the plates was hot rolled to 15 mm. For the alloy according to the invention, the hot rolling entry temperature was 467° C., the exit temperature at 40 mm was equal to 465° C. and at 15 mm was 444° C.

[0088] Plates were put into solution heat treatment under the following conditions:

[0089] 3 h and 6 h at 497° C. for 2024 plates with thicknesses equal to 15 and 40 mm respectively,

[0090] 2 h and 5 h at 499° C. for 2034 plates with thicknesses equal to 15 and 40 mm,

[0091] 9 h at 497° C. for plates according to the invention.

[0092] After quenching in cold water, all plates were subjected to controlled stretching to give a permanent elongation of 2%.

[0093] The static mechanical characteristics in the L and TL directions were then measured, to determine the ultimate stress R_(m) (in MPa), the conventional yield stress at 0.2% R_(0.2) (in MPa) and elongation at failure A (in %). The results are given in table 2: TABLE 2 Alloy Thickness Direction R_(m) R_(0.2) A 2024 40  L 468 362 20.0 2024 40 TL 469 330 17.4 2024 15  L 462 360 21.2 2024 15 TL 467 325 17.6 2034 40  L 534 416 11.2 2034 40 TL 529 393 12.0 2034 15  L 548 431 13.8 2034 15 TL 531 395 14.6 Invention 40  L 510 384 15.4 Invention 40 TL 475 336 18.9 Invention 15  L 501 390 16.7 Invention 15 TL 491 351 19.1

[0094] The toughness was also measured by critical intensity factors in plane stress K_(c) and Ke₀ (in MPa{square root}m) in the L-T direction according to ASTM standard E 561, on CCT test pieces sampled at quarter thickness, with width W=500 mm and thickness B=5 mm, and a central notch machined by electroerosion 2a₀=165 mm, enlarged to 170 mm by a fatigue test. Table 3 contains the results: TABLE 3 Alloy Thickness K_(c) K_(c0) 2024 40 143.4 105.2 2034 40 128.8 97.8 Invention 40 179.7 122 2034 15 136.4 103.7 Invention 15 173.6 124.3

[0095] The fatigue crack propagation rate da/dn was also measured in the L-T direction (in mm/cycle) for different values of the ΔK (in MPa{square root}m) according to ASTM standard E 647. This was done using two CCT samples with width W=200 mm and thickness B=5 mm, sampled at a quarter-plate thickness in the L-T direction. The length of the central notch machined by electroerosion is 30 mm, and this notch is enlarged by the fatigue test to 40 mm. The crack rate measurement test is carried out on an MTS machine with a load at R=0.05 and a stress of 40 MPa, calculated to give a value of ΔK equal to 10 MPa{square root}m for the initial notch length of 40 mm (results in table 4). TABLE 4 Alloy Thickness ΔK = 10 ΔK = 12 ΔK = 15 ΔK = 20 ΔK = 25 2024 40 9 10⁻⁵ 1.5 10⁻⁴ 3.0 10⁻⁴ 6 10⁻⁴ 9 10⁻⁴ 2034 40 3 10⁻⁵ 1.5 10⁻⁴ 3 10⁻⁴ 5.7 10⁻⁴ 1.7 10⁻³ Invention 40 5.5 10⁻⁵ 1.7 10⁻⁴ 2.0 10⁻⁴ 4.0 10⁻⁴ 7.8 10⁻⁴ 2034 15 8 10⁻⁵ 1.5 10⁻⁴ 3 10⁻⁴ 5.2 10⁻⁴ 2.1 10⁻³ Invention 15 4.9 10⁻⁴ 6.0 10⁻⁴ 1.3 10⁻⁴ 2.5 10⁻⁴ 5.4 10⁻⁴

[0096] Fatigue tests according to the Airbus specification AITM 1-0011 were carried out on 7.94 mm thick perforated test pieces 230 mm long, 50 mm wide, sampled at mid-thickness in the plate in the L direction. The hole diameter is 7.94 mm. An average stress of 80 MPa on the solid test pieces was applied with four alternating stress levels; 85 MPa, 55 MPa, 45 MPa and 35 MPa for 40 mm plates, and with stresses of 110, 85, 55 and 45 MPa for 15 mm plates, with 2 test pieces per level. The average life values (as a number of cycles) are given in table 5. It is found that the fatigue life is more than 200 better than with alloy 2024, with a notch factor K_(t)=2.5. TABLE 5 Thickness 80 ± 85 80 ± 55 80 ± 45 80 ± 35 Alloy mm MPa MPa MPa MPa 2024 40 36044 159721 2034 40 30640 125565 340126  839340 Invention 40 42933 219753 392680 1018240 2034 15 41040 204038 352957 Invention 15 45841 241932 429895

[0097] Finally, the deflections f in the L and TL direction were measured, together with the recrytallization rate (in %) at the surface, at a quarter thickness and at half-thickness, determined by image analysis after chemical etching of the sample.

[0098] The deflection f is measured as follows. Two bars are taken from the plate with thickness e, one called the L direction bar with length b in the direction of the length of the plate (L direction), 25 mm wide in the direction of the width of the plate (TL direction) and with thickness e equal to the full thickness of the plate (TC direction), the other bar being called the TL direction bar with dimensions of 25 mm in the L direction, b in the TL direction and e in the TC direction.

[0099] Each bar is machined down to half-thickness and the deflection at mid-length of the bar is measured. This deflection is representative of the internal stresses in the plate and its ability to not deform during machining. The distance 1 between supports was 180 mm and the length b of the bars was 200 mm. Machining was done mechanically and progressively with passes of about 2 mm. The deflection at mid-length was measured using a dial gauge with a resolution of one micron. The results of the deflections and recrystallization rates are shown in table 6. TABLE 6 Work Work Work hard. hard. hard. Thick- ratio ratio ratio Alloy ness f_(L) (μm) f_(TL) (μm) (surf.) % (¼ t) % (½ t) % 2024 40 210 120 79 58 30 2034 40 147 129 12 0 0 Inven- 40 86 75 46 5 2 tion 

1. Rolled, extruded or forged product made of an AlCuMg alloy processed by solution heat treatment, quenching and cold stretching, to be used in the manufacture of aircraft structural elements, with the following composition (% by weight): Fe<0.15 Si<0.15 Cu: 3.8-4.4 (preferably: 4.0-4.3) Mg: 1-1.5 Mn: 0.5-0.8 Zr: 0.08-0.15 other elements: <0.05 each and <0.15 total with a ratio R_(m)(L)/R_(0.2)(L)>1.25 (and preferably >1.30).
 2. Product according to claim 1, characterized in that Fe+Si<0.15%
 3. Rolled product between 6 and 60 mm thick according to one of claims 1 or 2, with an ultimate tensile strength R_(m(L)) in the quenched and stretched temper >475 MPa and yield stress R_(0.2) (L)>370 MPa.
 4. Rolled product between 6 and 60 mm thick according to any one of claims 1 to 3, with a plastic range between the ultimate tensile strength R_(m) and the yield stress R_(0.2) in the L and TL directions in the quenched and stretched temper >100 MPa.
 5. Rolled product between 6 and 60 mm thick according to any one of claims 1 to 4, for which the critical intensity factor (L-T direction) K_(c) in the quenched and stretched temper >170 MPa{square root}m and K_(co)>120 MPa{square root}m measured according to ASTM standard E 561 on notched test pieces sampled at a quarter thickness with parameters W=500 mm, B=5 mm and 2_(B0)=165 mm).
 6. Rolled product according to any one of claims 1 to 5, characterized in that it has a critical intensity factor (L-T direction) K_(c) or K_(c0) at least 100 higher than alloy 2024 under the same conditions.
 7. Rolled product according to any one of claims 1 to 6, characterized in that the crack propagation rate (L-T direction) da/dn in the quenched and stretched temper, measured according to ASTM standard E 647 on notched test pieces sampled at a quarter thickness with parameters W=200 mm and B=5 mm) is as follows: <10⁻⁴ mm/cycle for ΔK=10 MPa{square root}m <2.5 10⁻⁴ mm/cycle for ΔK=15 MPa{square root}m and <5 10⁻⁴ mm/cycle for ΔK=20 MPa{square root}m
 8. Rolled product according to any one of claims 1 to 7, characterized in that deflection f is measured in the L and TL directions after machining a bar supported on two supports separated by a length 1 to its mid-thickness <(0.14 1²)/e, where f is measured in microns, e is the thickness of the plate and 1 is the length measured in mm.
 9. Rolled product according to any one of claims 3 to 8, characterized in that the average fatigue life measured on a notched sample taken at mid-thickness in the L direction is more than 20% better than with the 2024 alloy.
 11. Process according to any one of claims 1 to 9 for manufacturing a product comprising the following steps: cast a plate with the indicated composition, homogenize this plate between 450 and 500° C., hot transformation, and possibly cold transformation by rolling, extrusion or forging, until the required product is obtained, solution heat treatment at a temperature of between 480 and 505° C., quench in cold water, cold stretching to at least 1.5% permanent deformation, natural aging under ambient conditions.
 12. Process according to claim 10, characterized in that the hot transformation takes place with an exit temperature >420° C. and preferably >440° C.
 13. Use of plates according to one of claims 3 to 9 for manufacturing the skin of an aircraft lower wing.
 14. Use of profiles according to one of claims 1 or 2, for manufacturing aircraft lower wings or fuselage stringers. 